Nickel and iron-based alloys are important structure and cladding materials for modern nuclear reactors due to their high mechanical properties and high corrosion resistance. To understand the radiative and corrosive environment influence on the mechanical strength, computer simulation works are conducted. In particular, this dissertation is focused on multiscale modeling of the effects of radiation-induced solute segregation and oxidation on grain boundary (GB) strength in nickel-based and iron-based alloys. Besides the atomistic scale density functional theory (DFT) based calculations of GB strength, continuum-scale cohesive zone model (CZM) is also used to simulate intergranular fracture at the microstructure scale. First, the effects of solute or impurity segregation at GBs on the GB strength are studied. Thermal annealing or radiation induced segregation of solute and impurity elements to GBs in metallic alloys changes GB chemistry and thus can alter the GB cohesive strength. To understand the underlying mechanisms, first principles based DFT calculations are conducted to study how the segregation of substitutional solute and impurity elements (Al, C, Cr, Cu, P, Si, Ti, Fe, which are present in Ni-based X-750 alloys) influences the cohesive strength of Σ3(111),Σ3(112),Σ5(210) and Σ5(310) GBs in Ni. It is found that C and P show strong embrittlement potencies while Cr and Ti can strengthen GBs in most cases. Other solute elements, including Si, have mixed but insignificant effects on GB strength. In terms of GB character effect, these solute and impurity elements modify the GB strength of the Σ5(210) GB most and that of the Σ3(111) least. Detailed analyses of solute-GB chemical interactions are conducted using electron localization function, charge density map, partial density of states, and Bader charge analysis. The results suggest that the bond type and charge transfer between solutes and Ni atoms at GBs may play important roles on affecting the GB strength. For non-metallic solute elements (C, P, Si), their interstitial forms are also studied but the effects are weaker than their substitutional counterparts. Nickel-base alloys are also susceptible to stress corrosion cracking (SCC), in which the fracture mainly propagates along oxidized grain boundaries (GBs). To understand how oxidation degrades GB strength, the next step is to use density functional theory (DFT) calculations to study three types of oxidized interfaces: partially oxidized GBs, fully oxidized GBs, and oxide/metal interface, using Ni as a model system. For partially oxidized GBs, both substitutional and interstitial oxygen atoms of different concentrations are inserted at three Ni GBs: Σ3(111) coherent twin, Σ3(112) incoherent twin, and Σ5(210). Simulation results show that the GB strength decreases almost linearly with the increasing oxygen coverage at all GBs. Typically, substitutional oxygen causes a stronger embrittlement effect than interstitial oxygen, except at the Σ3(111). In addition, the oxygen-induced mechanical distortion has a much smaller contribution to the embrittlement than its chemical effect, except for oxygen interstitials at the Σ3(111). For the fully oxidized GBs, three NiO GBs of the same types are studied. Although the strengths of Σ3(112) and Σ5(210) NiO GBs are much weaker than the Ni counterparts, the Σ3(111) NiO GB has a higher strength than that in Ni, indicating that Σ3(111) GB may be difficult to fracture during SCC. Finally, the strength of a Ni/NiO interface is found to be the weakest among all interfaces studied, suggesting the metal/oxide interface could be a favorable crack initiation site when the tensile stress is low. Furthermore, the effects of co-segregation of oxygen and solute/impurity elements on GB strength are studied by DFT, using the 5(210) GB in an face-centered-cubic (FCC) Fe as a model system. Four elements (Cr, Ni, P, Si) that are commonly present in stainless steels are selected. Regarding the effects of single elements on GB strength, Ni and Cr are found to the increase the GB strength, while both P and Si have embrittlement effects. When each of them is combined with oxygen at the GB, the synergetic effect can be different from the linear sum of individual contributions. The synergetic effect also depends on the spatial arrangement of solute elements and oxygen. If they are aligned on the same plane at the GB, the synergetic effect is similar to the linear sum, although P and Si show stronger embrittlement potencies when they combine with both interstitial and substitutional oxygen. When they are arranged on a trans-plane structure, only nickel combined with oxygen show larger embrittlement potencies than the linear sum in all cases. Crystal Orbital Hamilton Populations analysis of bonding and anti-bonding states is conducted to interpret how the interaction between solutes and oxygen impacts GB strength. Finally, the continuum-scale CZM method, which is based on the bilinear mixed mode traction separation law, is used to model SCC-induced intergranular fracture in polycrystalline Ni and Fe based alloys in the MOOSE framework. The previous DFT results are used to justify the input parameters for the oxidation-induced GB strength degradation. In this study, it is found that the crack path does not always propagate along the weak GBs. As expected, the fracture prefers to occur at the GB orientations perpendicular to the loading direction. In addition, triple junctions can arrest or deflect fracture propagation, which is consistent with experimental observations. Simulation results also indicate that percolated weak GBs will lead to a much lower fracture stress compared to the discontinuous ones. / Doctor of Philosophy / Iron and Nickel based alloys are important structural materials for nuclear reactors due to their good mechanical properties, corrosion resistance, and radiation resistance. Under radiation and corrosive conditions, those alloys are susceptible to radiation induced segregation (RIS) and stress corrosion cracking (SCC). This dissertation is mainly focused on understanding the influence of the two effects on grain boundary (GB) strength. Systematic atomistic scale density functional theory (DFT) simulations are applied for the nickel and iron systems. Based on the DFT results, cohesive zone model is utilized for the continuum scale fracture simulation in nickel and iron polycrystal. First, DFT calculations are conducted for studying the RIS effect on the GB strength in nickel. Al, Cr, Cu, C, Si, P, Fe, and Ti are chosen as segregated element. Σ3(111), Σ3(112), Σ5(210), Σ5(310) four types of GBs are built for GB strength calculations. It is found that substitutional C and P always embrittle the GB, while substitutional Ti and Cr can strengthen the GB in most cases. Partial density of states (PDOS) analysis indicates the formation of C-Ni and P-Ni covalent bonds is the possible reason for their embrittlement effects. Bader charge analysis shows negatively charged elements likely reduce the GB strength. Interstitial element segregation is applied for non-metal elements (C, P, and Si). The results indicate interstitial elements have weaker effects than substitution ones. On the next stage to study the SCC effect, DFT calculations are performed for nickel Σ3(111), Σ3(112), and Σ5(210) GBs with difference oxygen concentration and oxygen incorporation types. Besides partially oxidized GBs, fully oxidized GBs (NiO GBs) and metal-oxide interface are also constructed for comparison. Simulation results show that the GB strength decreases nearly monotonically as oxygen concentration goes up. Typically, substitution oxygen causes a larger embrittlement effect than interstitial oxygen except at Σ3(111). It is found that the large mechanical distortion in this coherent twin GB contributes significantly to the GB strength drop. NiO GBs can be weak (Σ3(112),Σ5(210)) or strong (Σ3(111)). NiO/Ni interface shows lowest strength compared with partially and fully oxidized GBs, indicating the importance of the metal-oxide interface in the SCC process. Furthermore, the combined effects between segregated elements and oxygen are studied in face center cubic (FCC) iron system. In this part only Σ5(210) GB is selected with substitutional Cr, Ni, P, and Si as segregated elements. The results of single element effects show Cr can strength the GB while P has an opposite effect. Other two elements show little effect. For the co-segregation effects, the trans-plane structures have larger embrittlement potencies than in-plane ones for Ni, suggesting the GB strength can also be affected by the spatial arrangement of segregated elements. Finally, cohesive zone model is applied for fracture simulations in polycrystalline nickel and iron under tensile loading condition. It is found that intergranular fracture depends on both GB strength and orientation. GBs perpendicular to the loading direction have higher chances to crack. It is also found the percolated weak GBs induce larger strength drop than the discontinuous ones.

L’objectif de cette étude e est de comprendre le processus de déalliage de l’acier inoxydable austénitique 304L avec l’intention de transcrire ce raisonnement aux aciers duplex. Des essais ont été réalisés au sein d’une solution aqueuse désaérée d’hydroxyde de sodium à 50%, portés à une température de 80°C sous pression atmosphérique et à potentiel libre. - L’alliage 304L se dissout en formant une couche nanoporeuse riche en nickel métallique sur sa surface. - L’alliage 2202 se dissout et présente deux comportements différents : o la ferrite s’appauvrit en nickel o l’austénite se recouvre d’une couche nanoporeuse constituée de nickel métallique. o les deux phases ont des vitesses de dissolution distinctes, l’austénite se dissolvant plus rapidement que la ferrite. Les cinétiques de dissolution des deux alliages sont différentes : l’alliage 2202 présente une meilleure résistance à la corrosion que l’alliage 304L. Cependant l’austénite de l’alliage 2202 se comporte de manière identique à l’alliage 304L et présente les mêmes caractéristiques. La ferrite semble conférer à l’alliage duplex une protection contre la corrosion caustique au détriment de l’austénite.La mise en évidence de la couche du nickel métallique presque pur est confrontée avec des modèles existants de déalliage. Des expériences complémentaires ont prouvées la simultanéité des étapes de dissolution de l'alliage, de la redéposition des atomes de Ni et de leur réarrangement sur la surface. / The aim of this study is to understand the process of dealloying of austenitic stainless steel 304L with the intention to put this reasoning to the duplex steels. Tests were conducted in a deaerated aqueous solution of sodium hydroxide at 50%, heated to a temperature of 80°C at atmospheric pressure and free potential. • The alloy 304L is dissolved to form a nanoporous layer rich in nickel metal on its surface. • The alloy 2202 is dissolved and has two different behaviors: o Ferritic phase is depleted in nickel o Austenite is covered by a nanoporous layer consists of metallic nickelo The two phases have different dissolution rates: austenite dissolves faster than ferrite. Kinetic dissolution of two alloys is different: alloy 2202 has better corrosion resistance than alloy 304L. However, the behavior of the austenite of the alloy 2202 is identical to the alloy 304L and has the same characteristics. The ferrite appears to give the duplex alloy corrosion protection against caustic at the expense of austenite. The identification of the layer of almost pure metallic nickel is confronted with existing models of dealloying. Additional experiments proved the simultaneous steps of dissolution of the alloy, redeposition of Ni atoms and their rearrangement on the surface.

Les aciers inoxydables lean duplex, à faible teneur en nickel et sans molybdène, représentent une alternative économique pour les usines de dessalement et l’industrie pétrolière. Celles-ci ont la particularité d’être exposées à des milieux très agressifs dont la présence de chlorure, de sulfure d’hydrogène, de hautes températures ou encore d’acides peut provoquer des phénomènes de fissuration sous contrainte.Cette étude est divisée en deux parties, la première se consacre aux milieux purement chlorurés et la seconde aux milieux contenant du sulfure d’hydrogène. Dans les deux parties, la compréhension des phénomènes liés à la fissuration sous contrainte des lean duplex est effectuée sur la nuance S32304, puis est comparée aux comportements des nuances S32202 et S32101. L’influence des milieux bouillants sur la résistance à la fissuration des aciers inoxydables, les mécanismes de dépassivation et de dissolution sélective des lean duplex, les différents modes de fissuration en présence de sulfure d’hydrogène ou encore l’amorçage de la corrosion sous contrainte assistée par le sulfure d’hydrogène sont abordés dans ce rapport. / Lean duplex stainless steels, with low content of nickel and without molybdenum, represent an economic alternative for desalting plants and petroleum industry. For these uses, steel have the particularity to be exposed to very aggressive environments inducing phenomenon of Stress Corrosion Cracking as chlorides, hydrogen sulphur, high temperatures or acids.This study is divided in two parts dedicated to two different environments. The first part is devoted to chloride middles and the second to hydrogen sulphur middles. In both parts, the understanding of phenomenon linked to the stress corrosion cracking of lean duplex is studied on the grade steel S32304, then is compared to the behaviour of grade steels S32202 and S32101. The topics treated in this report are notably the influence of boiling environments on the cracking resistance of stainless steels, the mechanism of unpassivation and selective dissolution of lean duplex, the different modes of cracking in presence of hydrogen sulphur, and the initiation of stress corrosion cracking assisted by hydrogen sulphur

Re-processed oxide fuel product from the Thermal Oxide Reprocessing Plant (THORP) is stored in Type 316L stainless steel, using a design of several nested cans, with the outer can providing the safety case containment barrier. The research reported in this PhD thesis aims to support the safety case related to these storage cans, by identifying and characterising susceptible microstructure sites and associated material surface conditions. The overarching goal of this project is to understand the propensity of THORP storage cans towards localised corrosion and Environment Assisted Cracking (EAC) in HCl and chloride-bearing atmospheric environments. The investigation focused on two possible corrosion cases: (1) understanding the effect of surface finishing on material performance in chloride-containing atmospheric environments, and (2) characterising the effects of the HCl aqueous solutions inside the can, with potential formation of HCl vapour. Microstructure investigations were carried out on surface-treated type 316L coupon specimens. The application of aqua blasting resulted in a deformed near-surface microstructure, containing compressive residual stresses to a depth of 100-120 micrometres. Subsequent laser engraving produced a recrystallized surface layer with tensile residual stresses reaching to a depth of 200 micrometres. Changes of surface roughness topography were accompanied by the development of a thick oxide/hydroxide film after laser engraving. Atmospheric exposure revealed similar corrosion attack for all samples, with laser engraving exhibiting the lowest number of corrosion sites, but with the largest average depth of attack. In addition, laser engraving led to atmospheric-induced stress corrosion cracking (AISCC) within two weeks of exposure to 386 ug/cm2 MgCl2-laden droplet deposits, with crack growth rates similar to ground U-bend samples. Strategies to reduce the likelihood of AISCC of laser-engraved components are discussed. The influence of HCl concentration and exposure temperature on the corrosion type and rate of annealed and cold rolled type 316L stainless steel has also been investigated. Cold rolling of up to 20 % reduction was introduced, with potentio-dynamic polarization measurements conducted in 0.01 - 3 M HCl aqueous solution. Results are compared to microstructures immersed under open circuit conditions, and to HCl-laden droplet deposits at temperatures up to 80C. Corrosion type diagrams are introduced to describe the transition between uniform corrosion, mixed-mode uniform with pitting corrosion, and pitting corrosion only, as a function of temperature, HCl concentration, and cold deformation. SCC tests of type 316L stainless steel have been carried out at 110C, by exposing U-Bend samples to HCl-laden droplets and HCl vapour. The humidity of the environment was controlled using defined volume fractions of H2O in a sealed environmental chamber. HCl-laden droplets with chloride deposition densities exceeding 1.5 ug/cm2 led to SCC after 90 minutes of exposure, whereas no corrosion attack was observed for samples with exposure to 0.15 ug/cm2 HCl. Increasing HCl concentrations resulted in fewer, but longer cracks, reaching up-to several hundreds of micrometres in length. HCl vapour exposure was carried out by adding various volumes of HCl solution in a beaker to the sealed test chambers. These HCl vapour tests confirmed a change of corrosion type with HCl concentration, from pitting corrosion with SCC, to the occurrence of uniform corrosion.

Primary Water Stress Corrosion Cracking (PWSCC) of Alloy 600 and similar Ni-Cr-Fe alloys is regarded as one of the most important challenges to nuclear power plant operation. During the past decades the majority of research has focused on PWSCC crack growth rate measurements in order to assess the lifetime of real components and to develop empirical models for crack propagation. However, the incubation and initiation stages of PWSCC have the same or even greater importance than the propagation stage, particularly because SCC can be undetected for more than 20 years before the occurrence of a rapid and catastrophic failure. There is, therefore, the scientific need to understand the mechanisms playing a fundamental role in the formation and development of intergranular cracks embryo, the so-called SCC initiation "precursor events", in order to be able to predict and mitigate the occurrence of PWSCC. Amongst all the models proposed for SCC initiation, the internal oxidation mechanism proposed by Scott and Le Calvar in 1992 appears to be the most comprehensive. Although the internal oxidation mechanism is widely accepted, it still requires further elucidation, especially in terms of enhanced grain boundary diffusivity and the role of intergranular carbides on the oxidation mechanism. The present work has focused on the initial stages of intergranular oxidation of solution-annealed (SA) and thermally-treated (TT) Alloy 600 with the aim of understanding the active mechanism responsible for the enhanced intergranular oxide penetration kinetics. The material was tested in simulated PWR primary water at 320°C, high-pressure hydrogenated-steam at 400°C and low-pressure H2-steam environment at 480°C at potential more reducing than the Ni/NiO equilibrium. The detailed microstructural characterization was conducted using scanning electron microscopy (SEM), transmission electron microscopy (TEM) and analytical transmission electron microscopy (ATEM) and demonstrated that Alloy 600SA is susceptible to diffusion-induced grain boundary migration (DIGM), preferential intergranular oxidation (PIO) and localised Cr and Fe depletions at the grain boundaries. The similar analyses performed on Alloy 600TT demonstrated reduced susceptibility to PIO and grain boundary migration. Further, detailed analyses confirmed that intergranular carbides were readily oxidized/consumed in all 3 environments and acted as Cr reservoir/O trap. These results shed additional light on the "precursor events" for PWSCC of Alloy 600, especially on the mechanism responsible for the enhanced Cr and O diffusivity and on the mechanism responsible for the enhanced Alloy 600TT SCC initiation resistance. Moreover, the strong similarities in the Alloy 600 oxidation behaviour observed for the 3 different environments and at the 3 different temperatures suggested that the same PIO mechanism is active in both steam and water and at temperatures between 320°C and 480°C. These results strongly support the possibility of using the low-pressure H2-steam environment as a substitute environment to accelerate PWSCC initiation without changing the mechanism.

Os aÃos inoxidÃveis austenÃticos tÃm sido bastante utilizados em equipamentos de utilidades de dessulfurizaÃÃo de petrÃleo devido à sua boa resistÃncia à corrosÃo em temperatura elevada.Contudo, esses materiais estÃo sujeitos a sensitizaÃÃo (deficiÃncia em cromo na regiÃo vizinha ao contorno de grÃo) quando expostos a temperaturas de 425 a 815ÂC, durante a operaÃÃo ou processos de fabricaÃÃo. A sensitizaÃÃo torna o equipamento suscetÃvel à corrosÃo sob tensÃo causada por aÃos politiÃnicos, formados pela interaÃÃo de compostos sulforoso, umidade e ar em temperatura ambiente. A resistÃncia à corrosÃo sob tensÃo de amostras de aÃo inoxidÃvel austenÃtico AISI 321 e 347, removidas de um tubo, foi investigada atravÃs do procedimento ASTM 262 Pr. E â ensaio alternativo e de execuÃÃo mais fÃcil do que a simulaÃÃo dos aÃos politiÃnicos. Os corpos de prova foram submetidos aos tratamentos tÃrmicos de estabilizaÃÃo (900ÂC, durante 75 minutos) e de sensitizaÃÃo (600ÂC, durante 20, 40, 80, 120 e 140 horas), apÃs o que foram expostos ao meio corrosivo de CuSO4 + H2SO4 durante 72 horas e depois dobradas, nÃo apresentando trincamento. A agressividade do meio utilizado no ensaio foi verificada atravÃs da utilizaÃÃo de amostras de aÃo AISI 304L sensitizadas (600ÂC, 24, 28 e 72 horas e 677ÂC durante 4, 45 e 72 horas). Neste caso, somente as amostras com acabamento superficial feito com lixa n 100 sofreram um intensivo processo corrosivo. / Os aÃos inoxidÃveis austenÃticos tÃm sido bastante utilizados em equipamentos de utilidades de dessulfurizaÃÃo de petrÃleo devido à sua boa resistÃncia à corrosÃo em temperatura elevada.Contudo, esses materiais estÃo sujeitos a sensitizaÃÃo (deficiÃncia em cromo na regiÃo vizinha ao contorno de grÃo) quando expostos a temperaturas de 425 a 815ÂC, durante a operaÃÃo ou processos de fabricaÃÃo. A sensitizaÃÃo torna o equipamento suscetÃvel à corrosÃo sob tensÃo causada por aÃos politiÃnicos, formados pela interaÃÃo de compostos sulforoso, umidade e ar em temperatura ambiente. A resistÃncia à corrosÃo sob tensÃo de amostras de aÃo inoxidÃvel austenÃtico AISI 321 e 347, removidas de um tubo, foi investigada atravÃs do procedimento ASTM 262 Pr. E â ensaio alternativo e de execuÃÃo mais fÃcil do que a simulaÃÃo dos aÃos politiÃnicos. Os corpos de prova foram submetidos aos tratamentos tÃrmicos de estabilizaÃÃo (900ÂC, durante 75 minutos) e de sensitizaÃÃo (600ÂC, durante 20, 40, 80, 120 e 140 horas), apÃs o que foram expostos ao meio corrosivo de CuSO4 + H2SO4 durante 72 horas e depois dobradas, nÃo apresentando trincamento. A agressividade do meio utilizado no ensaio foi verificada atravÃs da utilizaÃÃo de amostras de aÃo AISI 304L sensitizadas (600ÂC, 24, 28 e 72 horas e 677ÂC durante 4, 45 e 72 horas). Neste caso, somente as amostras com acabamento superficial feito com lixa n 100 sofreram um intensivo processo corrosivo. / Because of their resistance to high temperature corrosion by hydrogen sulfide, austenitic stanless steels are commonly used for equipment in desulfurization process. However, these materials are subject to sensitization (chromium carbide precipitation) from exposure in the temperature range 425 to 815ÂC during fabrication or operation. Sensitization makes the equipment susceptible to failure from intergranular stress corrosion cracking caused by polythionic acid. Polythionic acid is formed by sulfur compounds, moisture, and air at ambient temperature. The main goal of the present work is to investigate the stress corrosion cracking susceptibility of stainless steels AISI 321 and 347 in polythionic acids using an alternative process that is to submit the samples to cooper-cooper sulfate-16% sulfuric acid test (ASTM A262 Pr.E). After the stabilization heat treatment at 900ÂC for 75 minutes, samples were heat treated at 600ÂC during 20, 40, 80, 120 and 140 hours and then exposed to boiling acidified copper sulfate solution for 72 hours. After exposure, the specimens were bent. The appearance of fissures or cracks was not observed in AISI 321 and 347 samples. The effectiveness of the solution has been made by submitting AISI 304L samples to the same environment . The AISI 304L samples with higher finishing have been cracked. The ones with fine-ground finishing have not been attacked. / Because of their resistance to high temperature corrosion by hydrogen sulfide, austenitic stanless steels are commonly used for equipment in desulfurization process. However, these materials are subject to sensitization (chromium carbide precipitation) from exposure in the temperature range 425 to 815ÂC during fabrication or operation. Sensitization makes the equipment susceptible to failure from intergranular stress corrosion cracking caused by polythionic acid. Polythionic acid is formed by sulfur compounds, moisture, and air at ambient temperature. The main goal of the present work is to investigate the stress corrosion cracking susceptibility of stainless steels AISI 321 and 347 in polythionic acids using an alternative process that is to submit the samples to cooper-cooper sulfate-16% sulfuric acid test (ASTM A262 Pr.E). After the stabilization heat treatment at 900ÂC for 75 minutes, samples were heat treated at 600ÂC during 20, 40, 80, 120 and 140 hours and then exposed to boiling acidified copper sulfate solution for 72 hours. After exposure, the specimens were bent. The appearance of fissures or cracks was not observed in AISI 321 and 347 samples. The effectiveness of the solution has been made by submitting AISI 304L samples to the same environment . The AISI 304L samples with higher finishing have been cracked. The ones with fine-ground finishing have not been attacked.

Increased equipment failures and the resultant increase in unplanned downtime as the result of process optimization programs continue to plague pulp mills. The failures are a result of a lack of understanding of corrosion in the different pulping liquors, specifically the parameters responsible for its adjustment such as the role and identification of inorganic and organic species. The current work investigates the role of inorganic species, namely sodium hydroxide and sodium sulfide, on liquor corrosivity at a range of process conditions beyond those currently experienced in literature. The role of sulfur species, in the activation of corrosion and the ability of hydroxide to passivate carbon steel A516-Gr70, is evaluated with gravimetric and electrochemical methods. The impact of wood chip weathering on process corrosion was also evaluated. Results were used to identify black liquor components, depending on the wood species, which play a significant role in the activation and inhibition of corrosion for carbon steel A516-Gr70 process equipment. Further, the effect of black liquor oxidation on liquor corrosivity was evaluated. Corrosion and stress corrosion cracking performance of selected materials provided information on classes of materials that may be reliably used in aggressive pulping environments.

Joints between carbon steel and Alloy 600, containing Alloy 82 weld metal, were exposed to two steam-hydrogen environments considered to simulate exposure to primary water conditions in a Pressurized Water Reactor (PWR) or Canada Deuterium Uranium (CANDU) reactor. The welds were found to have elevated and variable iron contents due to dilution by carbon steel during welding. This gave the Alloy 82 weld, near the inner surface of the component, an iron content approaching that of Alloy 800. A potentially protective external iron oxide film formed on the inner surface of the weld. However, the chromium content throughout the weld is below that which would form an external chromium oxide. The results indicate that low chromium content causes internal oxidation throughout the weld and potentially below the external iron oxide which could lead to Primary Water Stress Corrosion Cracking (PWSCC).

Joints between carbon steel and Alloy 600, containing Alloy 82 weld metal, were exposed to two steam-hydrogen environments considered to simulate exposure to primary water conditions in a Pressurized Water Reactor (PWR) or Canada Deuterium Uranium (CANDU) reactor. The welds were found to have elevated and variable iron contents due to dilution by carbon steel during welding. This gave the Alloy 82 weld, near the inner surface of the component, an iron content approaching that of Alloy 800. A potentially protective external iron oxide film formed on the inner surface of the weld. However, the chromium content throughout the weld is below that which would form an external chromium oxide. The results indicate that low chromium content causes internal oxidation throughout the weld and potentially below the external iron oxide which could lead to Primary Water Stress Corrosion Cracking (PWSCC).

In the present work, the effect of variation in specimen orientation and heat treatment on the Stress Corrosion Cracking (SCC) susceptibility of 7050 aluminum alloy was investigated in 3,5% NaCl solution and under freely corroding conditions. For this purpose, Constant Extension Rate Tests (CERT) was performed on precracked Compact Tension (CT) specimens and the Direct Current Potential Drop technique was applied to measure the crack lengths. In addition to crack length versus time curves, the relationship between the crack growth rate and the stress intensity factor was determined. Fractographic analysis was utilized extensively to support the findings related with basic mechanisms of cracking. The alloy was found to be in the most susceptible state in the SL orientation, in which the crack propagation direction is parallel to the rolling direction. The resistance to SCC is higher in the TS but at maximum in LT orientation where the loading direction is parallel to the rolling direction. In the peak aging treatment, T651, alloy is susceptible to SCC in SL orientation. When the over aging treatment, T7651, is applied the resistance is increased and the two step over aging treatment, T73651, has resulted in an additional improvement in this orientation. On the other hand, the alloy showed higher resistance to SCC in TS and LT orientations in T651 condition compared to the T7651 and T73651 treatments. In these orientations, the alloy is less susceptible in T73651 condition than in T7651 treatment.